CN114277327A

CN114277327A - Zirconium alloy plate texture adjusting method based on twin crystal induced recrystallization

Info

Publication number: CN114277327A
Application number: CN202111616618.7A
Authority: CN
Inventors: 邱日盛; 曾庆辉; 刘庆
Original assignee: Chongqing University
Current assignee: Chongqing University
Priority date: 2021-12-27
Filing date: 2021-12-27
Publication date: 2022-04-05
Anticipated expiration: 2041-12-27
Also published as: CN114277327B

Abstract

The invention discloses a zirconium alloy plate texture adjusting method based on twin crystal induced recrystallization, which comprises the following steps: step 1: and (3) rolling the zirconium alloy plate after heat preservation at the liquid nitrogen temperature, wherein any one of A, B is adopted: A. selecting the rolling direction of the original plate in the normal direction of the rolling surface, wherein the rolling direction is along the normal direction or the transverse direction of the original plate; B. selecting the original plate to be transverse in the rolling surface normal direction, wherein the rolling direction is along the original plate normal direction or the rolling direction; the rolling total reduction is 10-40%, and the rolling pass reduction is 5-10%; step 2: carrying out vacuum annealing on the rolled and deformed zirconium alloy, wherein the temperature of the vacuum annealing is 550-600 ℃, and the annealing time is 25-35 min; or the rolled and deformed zirconium alloy sample is heated to 400 ℃ along with the furnace at the speed of 10 ℃/s, and then the annealing is carried out. The method has simple process flow, and the recrystallized structure zirconium alloy plate with weakened basal plane texture can be obtained only by slightly changing the existing zirconium alloy plate processing process.

Description

Zirconium alloy plate texture adjusting method based on twin crystal induced recrystallization

Technical Field

The invention relates to the technical field of metal processing, in particular to a zirconium alloy plate texture adjusting method based on twin crystal induced recrystallization.

Background

The zirconium alloy sheet is widely applied to nuclear reactors as a preparation material of a spacer grid due to excellent mechanical properties, a low neutron absorption cross section and excellent corrosion resistance.

Texture is also referred to as preferred orientation of grains, and means that the orientation of individual grains in a polycrystalline body tends to be uniform. The texture of the zirconium alloy as a fuel cladding affects not only the orientation of the hydrides in the zirconium alloy and numerous mechanical performance parameters such as mechanical strength, creep, plasticity, fatigue, etc., but also radiation growth, stress corrosion cracking, water side corrosion performance. The texture research and control of zirconium alloy are very important in the development and utilization of zirconium alloy.

The mechanical property and the corrosion resistance of the zirconium alloy plate produced in China can meet the application requirements of nuclear reactors. However, in the process of preparing the positioning grid by punching, the problem of punching cracking often occurs, and the problem can cause the mechanical property and the surface quality of the punched strip of the zirconium alloy sheet to be rapidly reduced, directly influences the service performance of the positioning grid and limits the industrial production of the domestic zirconium alloy positioning grid. The improvement of the forming performance of the zirconium alloy sheet is a main means for solving the problem of punching cracking, and the change of the content or the texture of the zirconium alloy elements is an important way for remarkably improving the forming performance of the zirconium alloy sheet. However, under the requirements of corrosion resistance and the like, the content of alloy elements cannot be changed greatly, so that the forming performance of the zirconium alloy sheet can be improved while other performances are not changed obviously by adjusting the texture of the zirconium alloy sheet.

At present, the texture of the zirconium alloy sheet is often adjusted in the industrial production by means of beta-alpha phase transformation, rolling deformation control in an alpha phase region, annealing treatment process parameters and the like. However, the sliding system is less in the hexagonal close-packed structure, so that the stable basal plane texture formed by the zirconium alloy sheet in the processing process is difficult to adjust. This situation restricts the development of the zirconium alloy thin plate made in China, so that a texture adjusting technology of the zirconium alloy thin plate must be developed.

Disclosure of Invention

The invention aims to provide a method for adjusting the texture of a zirconium alloy plate based on twin crystal induced recrystallization, which overcomes the defect that the texture of a basal plane of a zirconium alloy cannot be adjusted greatly in the prior art, is expected to improve the forming performance of the zirconium alloy plate and improve the processing and preparation capacity of the domestic zirconium alloy plate.

In order to achieve the purpose, the invention adopts the technical scheme that:

a zirconium alloy plate texture adjusting method based on twin crystal induced recrystallization comprises the following steps:

step 1: the zirconium alloy plate is rolled after heat preservation at the temperature of liquid nitrogen, and any one of the following two ways of A, B is adopted:

A. selecting a Rolling Direction (RD) of the original plate from the rolling surface Normal Direction (ND), wherein the rolling direction is along the original plate Normal Direction (ND) or the Transverse Direction (TD);

B. selecting the Transverse Direction (TD) of the original plate in the rolling surface Normal Direction (ND), wherein the rolling direction is along the original plate Normal Direction (ND) or the Rolling Direction (RD);

the rolling total reduction is 10-40%, the rolling pass reduction is 5-10%, and after each pass of rolling is finished, the rolled sample is placed into liquid nitrogen for soaking and heat preservation, and then the next rolling is carried out;

step 2: carrying out vacuum annealing on the rolled and deformed zirconium alloy:

the temperature of the vacuum annealing is 550-600 ℃, and the annealing time is 25-35 min; alternatively, the first and second electrodes may be,

firstly, heating a rolled and deformed zirconium alloy sample to 400 ℃ along with a furnace at the speed of 10 ℃/s for pre-recovery treatment, and then annealing at 550-600 ℃ for 25-35 min.

Preferably, the total rolling reduction in the step 1 is 15-20%.

Preferably, the heat preservation time of the zirconium alloy plate in liquid nitrogen is 20-30 min.

Further preferably, the time for keeping the zirconium alloy plate in the liquid nitrogen is 20 min.

Preferably, the annealing temperature in step 2 is 600 ℃ and the annealing time is 30 min.

Preferably, the diameter of the roller is 170mm, the rolling speed is 0.2m/s, the single-pass reduction is 5%, the total reduction is 3 passes, and the total reduction is 15%.

Preferably, the Rolling Direction (RD) of the zirconium alloy sheet material is the same as the Rolling Direction (RD) of the original sheet material, and the rolling plane Normal Direction (ND) is the Transverse Direction (TD) of the original sheet material.

Preferably, the Rolling Direction (RD) of the zirconium alloy sheet material is the Transverse Direction (TD) of the original sheet material, and the rolling plane Normal Direction (ND) thereof is the Rolling Direction (RD) of the original sheet material.

Preferably, the zirconium alloy plate is a Zr702 plate.

The invention has the beneficial effects that:

1. carrying out low-temperature rolling deformation by taking the transverse direction or the rolling direction of the zirconium alloy plate as a pressing direction to obtain the zirconium alloy plate containing a rich stretching twin crystal structure, wherein the basal plane texture of the zirconium alloy is obviously weakened; and (3) performing 550-600 ℃ vacuum annealing on the preset stretched twin crystal zirconium alloy, and keeping twin crystal orientation through recrystallization behavior at a twin crystal structure to finally adjust the zirconium alloy plate texture.

2. The rolling deformation in the low-temperature preset direction can greatly adjust the deformation texture of the zirconium alloy under the condition of small deformation, and reduces the plastic processing procedure and deformation.

3. The method has simple process flow, and can obtain the recrystallized structure zirconium alloy plate with weakened basal plane texture by only slightly changing the existing zirconium alloy plate processing process.

Drawings

FIG. 1 is a flow chart of the method of the present invention.

FIG. 2 is the original weave pattern of a Zr702 sheet.

Figure 3 is a schematic view of the direction of cut of different rolled samples on a raw sheet.

FIG. 4 is a microstructure diagram of a sample No. 4 after rolling deformation.

FIG. 5 is a weave pattern of sample No. 1 after rolling deformation.

FIG. 6 is a view showing the microstructure of a rolled and deformed sample after annealing treatment.

FIG. 7 is a weave pattern of a rolled sample after annealing treatment.

FIG. 8 is a microstructure diagram of sample No. 2 after rolling deformation.

FIG. 9 is a weave pattern of sample No. 2 after rolling deformation.

FIG. 10 is a microstructure view of the rolled and deformed sample after annealing treatment.

FIG. 11 is a weave pattern of the rolled sample No. (C) (. II) after annealing treatment.

FIG. 12 is a microstructure diagram of the sample No. C after rolling deformation.

FIG. 13 is a weave pattern of sample No. C after rolling deformation.

FIG. 14 is a microstructure view of a rolled and deformed sample after annealing treatment.

FIG. 15 is a weave pattern of a No. rolling deformation sample after annealing treatment.

Detailed Description

The invention is further illustrated by the following examples, which are not intended to be limiting.

The experimental procedures in the following examples are conventional unless otherwise specified.

FIG. 1 is a flow chart of the method of the present invention, as shown in FIG. 1, comprising the steps of:

step 1: and (3) keeping the temperature of the zirconium alloy plate in the preset direction at the liquid nitrogen temperature, and then rolling to obtain the rolled deformed zirconium alloy plate. In the step, the heat preservation time of the zirconium alloy in liquid nitrogen is 20-30 min, so that a twin deformation system can be preferentially opened in the subsequent rolling deformation process. The rolling adopts any one of the following A, B modes:

the rolling total reduction is 10-40%, the rolling pass reduction is 5-10%, and after each pass of rolling is finished, the rolled sample is soaked in liquid nitrogen for 20-30 min, and then the next rolling is carried out;

the rolling total reduction is 10-40%, preferably 15-20% to retain twin crystal structure and twin crystal interface; the rolling pass reduction is 5-10%.

Step 2: and carrying out vacuum annealing on the rolled deformed zirconium alloy to obtain the zirconium alloy plate with the adjusted texture. In the step, the temperature of the zirconium alloy vacuum annealing is 550-600 ℃, and the annealing time is 30 min; or the sample is heated to 400 ℃ along with the furnace at the speed of 10 ℃/s for pre-recovery treatment, and then is annealed at 550-600 ℃ for 30min, and the annealing treatment mode can obtain a recrystallized grain structure with more uniform grain size.

Through the low-temperature preset direction rolling deformation in the step 1, a large number of twin crystal structures can be effectively introduced into the zirconium alloy sheet, and the orientation of the twin crystal structures can be kept from being changed remarkably due to small deformation amount, so that a large number of recrystallization nucleation positions are provided for the annealing treatment in the step 2. The vacuum annealing or pre-recovery annealing treatment process in the step 2 can enable most of recrystallized grains to keep twin crystal orientation, so that the basal plane texture of the zirconium alloy plate can be adjusted.

Example 1

The recrystallized Zr702 plate with basal plane texture is used as a raw material, and the Zr702 plate with the weakened basal plane texture is prepared through liquid nitrogen rolling deformation and annealing treatment. The chemical composition of the Zr702 plate is shown in table 1, and its original texture is shown in fig. 2.

TABLE 1 chemical composition of Zr702 plate (mass fraction%)

Zr+Hf

Hf

Nb

Fe+Cr

C

N

H

O

≥99.2

≤4.5

/

0.2

0.05

0.025

0.005

0.16

In order to realize rolling deformation along different directions of an original plate, in the embodiment, rolling samples are cut on the original plate according to the drawing shown in fig. 3, wherein samples I, II and III are cut, the size of the rolling sample is 50mm × 15mm × 2.6mm, and for three different rolling samples, the thickness direction of 2.6mm is taken as the normal direction of a rolling surface, the width direction of 15mm is taken as the transverse direction of rolling, and the length direction of 50mm is taken as the rolling direction.

The liquid nitrogen rolling deformation process comprises the following steps: mechanically polishing the surface of a small rolled sample in a preset direction until the surface is bright and flat, and then soaking the small rolled sample in liquid nitrogen for 20 min; and (3) rapidly carrying out rolling deformation on the soaked small rolled sample by a rolling mill along a preset direction, wherein the single-pass reduction is 5%, the diameter of a roller is 170mm, the rolling speed is 0.2m/s, after each pass of rolling is finished, the small rolled sample is continuously placed into liquid nitrogen to be soaked and insulated for 20min, the total rolling time is 3 passes, and the total reduction is about 15%.

The samples after the rolling deformation were vacuum annealed at 600 ℃ for 30min, and then air-cooled to room temperature.

Sample experiment of (I)

In this experiment, the rolling sample used was sample # i shown in fig. 3, and as described above, the rolling direction of the sample was the same as the original rolling direction of the plate material, i.e., the rolling direction was the original plate material RD, and the normal direction of the rolling plane was the original plate material ND. The microstructure after rolling deformation is shown in fig. 4, and it can be seen from the figure that only a very small amount of twin crystals are generated in the rolling deformation, and a large amount of low-angle grain boundaries indicate dislocation slip as a main deformation mechanism. The texture after rolling deformation is shown in FIG. 5, in which the crystal grain < c > axes are mainly distributed in the ND-TD plane, and most of the crystal grain < c > axes are deviated from ND to TD by 21 to 23 deg.

The microstructure of the annealed rolling deformation sample is shown in fig. 6, and it can be seen from the figure that the sample is recrystallized, and the density of the small-angle grain boundary is obviously reduced. The texture after annealing is shown in fig. 7, and similar to the deformed sample, the crystal grain < c > axes are mainly distributed in the ND-TD plane, and most of the crystal grain < c > axes are deflected by about 19 ° from ND to TD. In summary, in sample (i), dislocation glide weakens the basal plane texture of the original plate, but the weakening effect is small.

Sample experiment No.. 2

In this experiment, the rolling sample used was sample # m shown in fig. 3, and as described above, the rolling direction of the sample was the same as the original rolling direction of the plate material, i.e., the rolling direction was the original plate material RD, but the normal direction of the rolling surface was the original plate material TD. As shown in FIG. 8, the microstructure after the rolling deformation was observed, and a large number of {10-12} and {11-21} twin crystals were generated in the rolling deformation, and the twin deformation was the main deformation mechanism. The texture after rolling deformation is shown in FIG. 9, the crystal grain < c > axis is mainly distributed in the ND-TD plane, and most of the crystal grain < c > axis deviates from ND to TD by about 45 degrees because the twin crystal can significantly change the crystal orientation, for example, {10-12} stretching the twin crystal can rotate the crystal 85.22 degrees around the <11-20> axis.

The microstructure of the annealed rolled and deformed sample is shown in fig. 10, and it can be seen from the figure that the sample is recrystallized and the twin structure is completely replaced by equiaxed grains. The texture after annealing is shown in fig. 11, and similar to the deformed sample, the grains < c > axes are mainly distributed in the ND-TD plane, but most of the grains < c > axes are deflected by about 47-62 ° from ND to TD. The basal texture of the annealed samples was further weakened compared to the deformed samples. In conclusion, in sample II, a large amount of twin crystals are generated, so that the crystals are deflected at a large angle, the basal plane texture of the original plate is obviously weakened, and the basal plane texture is further weakened after annealing treatment.

Experiment on sample No. III

In this experiment, the rolling sample used was sample No. iii shown in fig. 3, and as described above, in this case, the rolling direction of the sample was the raw sheet TD, and the normal direction of the rolling surface was the raw sheet RD. As shown in FIG. 12, the microstructure after the rolling deformation was observed, and a large number of {10-12} and {11-21} twin crystals were generated in the rolling deformation, and the twin deformation was the main deformation mechanism. The texture after roll deformation is shown in FIG. 13, and the deformed sample has two texture components, namely a <0001>// ND texture component and a <0001>// RD texture component, wherein the <0001>// RD texture component is mainly caused by {10-12} stretching twins.

③ the microstructure of the rolled and deformed sample after annealing treatment is shown in fig. 14, and it can be seen from the figure that the twin structure in the deformed sample is completely replaced by the recrystallized grains with equiaxed shape. The annealed texture is shown in fig. 15, although the annealed texture is a weakened basal plane texture, the crystal grain < c > axis is deflected from ND to RD in the ND-RD plane by an angle of 38-46 °. In conclusion, in sample III, a new texture component, namely a <0001>// RD texture component, is generated in the deformed sample due to the generation of a large amount of stretching twin crystals, the basal plane texture of the original plate is obviously weakened, and after annealing treatment, the crystal grain < c > axis deflects from ND to RD in an ND-RD plane, and the weakening mode of the basal plane texture is different from that in experimental group 2.

Claims

1. A zirconium alloy plate texture adjusting method based on twin crystal induced recrystallization is characterized by comprising the following steps:

A. selecting an original plate rolling direction RD from the rolling surface normal direction ND, wherein the rolling direction is along the original plate normal direction ND or the transverse direction TD;

B. selecting the transverse TD of the original plate from the normal ND of the rolling surface, and rolling along the normal ND or RD of the original plate in the rolling direction;

2. The method of claim 1, wherein: the total rolling reduction in the step 1 is 15-20%.

3. The method of claim 1, wherein: the heat preservation time of the zirconium alloy plate in liquid nitrogen is 20-30 min.

4. The method of claim 3, wherein: the heat preservation time of the zirconium alloy plate in liquid nitrogen is 20 min.

5. The method of claim 1, wherein: the annealing temperature in the step 2 is 600 ℃, and the annealing time is 30 min.

6. The method of claim 1, wherein: the diameter of the roller is 170mm, the rolling speed is 0.2m/s, the single-pass reduction is 5 percent, the total rolling is 3 passes, and the total reduction is 15 percent.

7. The method of claim 1, wherein: the rolling direction RD of the zirconium alloy sheet is the same as the rolling direction RD of the original sheet, and the rolling plane normal direction ND is the original sheet transverse direction TD.

8. The method of claim 1, wherein: the rolling direction RD of the zirconium alloy sheet is the original sheet transverse direction TD, and the rolling plane normal direction ND thereof is the original sheet rolling direction RD.

9. The method of claim 1, wherein: the zirconium alloy plate is a Zr702 plate.